CN110933944B

CN110933944B - Diamond polycrystal and tool comprising same

Info

Publication number: CN110933944B
Application number: CN201880003674.3A
Authority: CN
Inventors: 角谷均; 山本佳津子
Original assignee: Sumitomo Electric Industries Ltd
Current assignee: Sumitomo Electric Industries Ltd
Priority date: 2018-07-20
Filing date: 2018-07-20
Publication date: 2022-10-18
Anticipated expiration: 2038-07-20
Also published as: US11427930B2; JP6421904B1; US20200340139A1; EP3825293A4; KR102552459B1; CN110933944A; WO2020017040A1; TWI704105B; KR20210031806A; TW202012309A; JPWO2020017040A1; EP3825293A1

Abstract

A diamond polycrystal, wherein a value of a ratio of d ' to d (d '/d) in a vickers hardness test conducted under conditions defined in JIS Z2244, 2009, is 0.98 or less, wherein d represents a length of a diagonal line of a first dimensional indentation formed in a surface of the diamond polycrystal when a vickers indenter having a test load of 4.9N is pressed against the surface of the diamond polycrystal, and d ' represents a length of a diagonal line of a second dimensional indentation left in the surface of the diamond polycrystal after the test load is released.

Description

Diamond polycrystal and tool comprising same

Technical Field

The present disclosure relates to diamond polycrystals and tools comprising the same.

Background

The diamond polycrystal has excellent hardness, no directionality of hardness, and no solvability. Therefore, diamond polycrystals are widely used in tools such as cutting tips, dressers and dies, and drill bits and the like.

A conventional diamond polycrystal is obtained by sintering diamond powder as a raw material together with a sintering aid and a binder at a high pressure and a high temperature (generally, a pressure of about 5GPa to 8GPa and a temperature of about 1300 ℃ to 2200 ℃) at which diamond is thermodynamically stable. Examples of useful sintering aids include: iron group element metals such as Fe, co or Ni; carbonates, e.g. CaCO ₃ (ii) a And the like. Examples of useful binders include ceramics, such as SiC。

The diamond polycrystal obtained by the method comprises a sintering aid and a bonding agent. The sintering aid and the binder may degrade mechanical properties such as hardness and strength and heat resistance of the diamond polycrystal.

The following diamond polycrystals are also known: removing the diamond polycrystal of the sintering aid by acid treatment; and diamond polycrystal using heat-resistant SiC as a binder to achieve excellent heat resistance. However, these diamond polycrystals have low hardness and low strength, and therefore have insufficient mechanical properties as a tool material.

Meanwhile, a non-diamond carbon material (such as graphite, glassy carbon, amorphous carbon, or onion-like carbon) can be directly converted into diamond at very high pressure and temperature without using a sintering aid or the like. The diamond polycrystal is obtained by sintering a non-diamond carbon material while directly converting the non-diamond phase into a diamond phase.

Japanese patent unexamined publication No.2015-227278 (patent document 1) discloses a technique in which a diamond polycrystal is obtained by directly converting non-diamond carbon powder into diamond at very high temperature and pressure (satisfying P ≧ 0.0000168T2-0.0876T +124, T ≦ 2300, and P ≦ 25, where P represents pressure (GPa) and T represents temperature (. Degree. C.)). In the obtained diamond polycrystal, the ratio b/a of the length a of the longer diagonal line to the length b of the shorter diagonal line of the knoop indentation in the knoop hardness measurement is 0.08 or less. The obtained diamond polycrystal has elasticity.

Japanese patent unexamined publication No.2018-008875 (patent document 2) discloses a technique in which an onion-like carbon as a raw material is directly converted into diamond by ultra-high temperature of 1200 to 2300 ℃ and ultra-high pressure of 4 to 25GPa to obtain an ultra-high hardness nano-twin crystal diamond bulk material having vickers hardness of 155 to 350GPa and vickers hardness of 140 to 240 GPa.

Reference list

Patent literature

Patent document 1: japanese patent unexamined publication No.2015-227278

Patent document 2: japanese patent unexamined publication No.2018-008875

Disclosure of Invention

[1] The diamond polycrystal of the present disclosure is a diamond polycrystal in which a value of a ratio (d '/d) of d' to d, where d represents a length of a diagonal line of a first dimensional indentation formed in a surface of the diamond polycrystal when a vickers indenter having a test load of 4.9N is pressed against the surface of the diamond polycrystal, is 0.98 or less in a vickers hardness test performed under conditions defined in JIS Z2244.

[2] The tool of the present disclosure is a tool comprising the diamond polycrystal described in [1 ].

Brief description of the drawings

Figure 1 shows a vickers indentation.

Detailed Description

[ problem to be solved by the present disclosure ]

The diamond polycrystal in patent document 1 has high hardness and high toughness, but further improvement in crack resistance is required.

The ultra-high hardness nano twin crystal diamond bulk material in patent document 2 has very high hardness, but insufficient toughness and insufficient crack resistance.

Accordingly, it is an object to provide a diamond polycrystal having excellent crack resistance and high fracture toughness while maintaining high hardness, and a tool comprising the diamond polycrystal.

[ advantageous effects of the present disclosure ]

According to the present disclosure, a diamond polycrystal having excellent crack resistance and high fracture toughness while maintaining high hardness, and a tool including the diamond polycrystal can be provided.

[ description of the embodiments ]

First, embodiments of the present disclosure are listed and described.

(1) A diamond polycrystalline body according to an embodiment of the present disclosure is a diamond polycrystalline body in which a value of a ratio of d 'to d (d'/d) in a vickers hardness test performed under conditions defined in JIS Z2244.

The diamond polycrystal has excellent crack resistance and high fracture toughness while maintaining high hardness.

(2) In the diamond polycrystal, the Vickers hardness calculated from the value of d is preferably 100GPa or more and less than 155GPa. The diamond polycrystal has high hardness and excellent wear resistance.

(3) In the diamond polycrystal, the Vickers hardness calculated from the value of d is preferably 120GPa or more and less than 155GPa. The diamond polycrystal has high hardness and thus more excellent wear resistance.

(4) Preferably, the diamond polycrystal is composed of a plurality of diamond particles, and the average particle diameter of the diamond particles is 100nm or less.

Therefore, the diamond polycrystal is suitably used for tools requiring excellent crack resistance and high fracture toughness, such as tools for high-load machining, micromachining and the like.

(5) A tool according to an embodiment of the present disclosure is a tool including the diamond polycrystal described in any one of (1) to (4).

The tool has excellent crack resistance and high fracture toughness when processing various materials.

[ detailed description of the embodiments of the present disclosure ]

Specific examples of diamond polycrystals and tools using the same according to an embodiment of the present disclosure are described below with reference to the accompanying drawings.

In the present specification, the expression "a to B" means a range from a lower limit to an upper limit (i.e., a to B). When a does not specify a unit but only B specifies a unit, the unit of a is the same as that of B.

[ Diamond polycrystal ]

In the diamond polycrystal according to the present embodiment, diamond is a basic composition. That is, the diamond polycrystal consists essentially of diamond, and substantially does not include a bonding phase (bonding agent) formed by one or both of the sintering aid and the bonding agent. Therefore, high hardness and strength can be achieved, thereby preventing deterioration of mechanical properties and particle shedding due to a difference in thermal expansion coefficient from the binder or catalytic action of the binder even under high temperature conditions.

Since the diamond polycrystal is a polycrystal composed of a plurality of diamond particles, the diamond polycrystal does not have anisotropy and solvability like a single crystal, but has isotropic hardness and wear resistance in all directions.

The diamond polycrystal of the present disclosure is defined by the absence of a diffraction peak originating from a structure other than a diamond structure, and in an X-ray diffraction spectrum obtained by X-ray diffraction, the integrated intensity of the diffraction peak is greater than 10% with respect to the total integrated intensity of all diffraction peaks originating from the diamond structure. That is, it can be confirmed that the diamond polycrystal does not contain the above-mentioned binder phase by X-ray diffraction spectroscopy. The integrated intensity of the diffraction peak is a value excluding the background. The X-ray diffraction spectrum can be obtained by the following method.

And grinding the diamond polycrystal by using a diamond grinding wheel, and taking the processing surface of the diamond polycrystal as an observation surface.

An X-ray diffraction spectrum of the machined surface of the diamond polycrystal was obtained using an X-ray diffractometer ("MiniFlex 600" (trademark), supplied by Rigaku). The conditions of the X-ray diffractometer in this case are, for example, as follows.

Characteristic X-ray: cu-K alpha (wavelength)

)

Tube voltage: 45KV

Tube current: 40mA

A filter: multilayer mirror

An optical system: concentration method

X-ray diffraction method: theta-2 theta method.

The diamond polycrystal may contain inevitable impurities as long as the effects of the present embodiment can be exhibited. Examples of the inevitable impurities include: less than 1ppm hydrogen; oxygen of 1ppm or less; nitrogen of 1ppm or less; and the like. In the present description, the concentration of unavoidable impurities refers to the concentration based on the number of atoms.

In order to improve the strength, the respective concentrations of hydrogen, oxygen, and nitrogen in the diamond polycrystal are preferably 1ppm or less, and more preferably 0.1ppm or less. Further, the total impurity concentration in the diamond polycrystal is preferably 3ppm or less, and more preferably 0.3ppm or less. The lower limit of the concentration of each of hydrogen, oxygen and nitrogen in the diamond polycrystal is not particularly limited, but is preferably 0.001ppm or more in view of production.

The respective concentrations of hydrogen, oxygen and nitrogen in the diamond polycrystal can be determined by Secondary Ion Mass Spectrometry (SIMS).

The diamond polycrystal in the present embodiment is a sintered body, but in many cases, the term "sintered body" is generally meant to include a binder, and thus the term "polycrystal" is used in the present embodiment.

(Diamond particle)

The average particle diameter of the diamond particles is preferably 100nm or less. Diamond polycrystal composed of diamond particles having such a small average particle diameter is suitably used for tools which are required to have excellent crack resistance and high fracture toughness, such as tools for high-load machining, micromachining and the like. When the average particle diameter of the diamond particles is greater than 100nm, the precision of the cutting edge may be reduced, resulting in easier breakage of the cutting edge. Therefore, the diamond polycrystal cannot be applied to a tool with high load and fine processing.

In order to make the diamond polycrystal suitable for a tool which requires a cutting edge having toughness and high accuracy, the average particle diameter of the diamond particles is more preferably 50nm or less, and still more preferably 20nm or less. From this viewpoint, the average particle diameter of the diamond particles may be 15nm or less, or may be 10nm or less.

In order to obtain mechanical strength peculiar to diamond, the lower limit of the average particle diameter of the diamond particles is preferably 1nm or more. From this viewpoint, the average particle diameter of the diamond particles may be 10nm or more, or may be 15nm or more.

The average particle diameter of the diamond particles is preferably 1nm to 100nm, more preferably 10nm to 60nm, and still more preferably 15nm to 50 nm.

The average particle diameter of the diamond particles can be determined by image observation using a Scanning Electron Microscope (SEM) of the surface of the diamond polycrystal which has been finished into a flat mirror surface by polishing. The specific method is as follows.

The surface of the diamond polycrystal polished to a flat mirror surface by a diamond wheel or the like is observed at a magnification of x1000 to x100000 times using a high-resolution scanning electron microscope, thereby obtaining an SEM image. As the high-resolution scanning electron microscope, for example, a field emission scanning electron microscope (FE-SEM) is preferably used.

Then, a circle is drawn on the SEM image, and then 8 straight lines are drawn radially (in such a manner that the included angles between the straight lines are substantially equal) from the center of the circle to the outer periphery of the circle. In this case, the observation magnification and the diameter of the circle are preferably set so that the number of diamond particles (grains) per straight line is about 10 to 50.

Then, the number of grain boundaries of the diamond particles passed through by each straight line was counted, then, the length of the straight line was divided by the number of passes to obtain an average intercept length, and then, the average intercept length was multiplied by 1.128, and the obtained value was regarded as an average particle diameter. The average particle diameter in each of the three SEM images was determined by the method described above, and the average of the average particle diameters of the three images was regarded as "average particle diameter of diamond particles".

In order to suppress the occurrence of micro cracks, the aspect ratio (A/B) of the major axis A and the minor axis B of each diamond particle in the SEM image is preferably 1. Ltoreq. A/B <4. Here, the major axis means a distance between two points on the contour line of the diamond particles, which are the largest in distance from each other. The short axis refers to a distance of a straight line which is orthogonal to a straight line defining the long axis and is longest between two intersection points with the profile of the diamond particle.

(Vickers hardness)

In the diamond polycrystal of the present embodiment, a value of a ratio of d ' to d (d '/d) in a vickers hardness test performed under conditions defined in JIS Z2244, 2009, is 0.98 or less, wherein d represents a length of a diagonal line of a first dimensional indentation formed in a surface of the diamond polycrystal when a vickers indenter having a test load of 4.9N is pressed against the surface of the diamond polycrystal, and d ' represents a length of a diagonal line of a second dimensional indentation left in the surface of the diamond polycrystal after the test load is released.

The vickers hardness test defined in JIS Z2244. The vickers hardness test is performed by pressing a vickers indenter against a target material at a predetermined temperature and a predetermined load (test load) to determine the hardness of the target material. In the present embodiment, the predetermined temperature is 23 ℃ ± 5 ℃, and the predetermined load is 4.9N.

The vickers indenter is an indenter made of diamond and has a shape of a regular quadrangular pyramid. In the vickers hardness test, the top side of the vickers indenter, opposite the bottom side, is pressed against the target material. In the present specification, the term "vickers indentation" is defined to mean including: a first dimensional indentation (see "first dimensional indentation" in fig. 1) which is a square indentation formed on the surface of a target material (diamond polycrystal in the present embodiment) when a vickers indenter is pressed against the surface of the target material at a predetermined temperature and a predetermined test load; and a second witness mark (see "second witness mark" in fig. 1), which is a permanent deformation mark left on the surface of the target material immediately after the test load is released.

In the case of a fully plastic body such as a general metal material, the first indentation when the vickers indenter is pressed has the same shape as the second indentation left after the vickers indenter is removed. The vickers indentations assume the same shape before and after the test load is released, and, for example, have a square shape shown by a broken line as a "first dimension indentation" in fig. 1. Thus, in a fully plastic body, d and d' are the same.

On the other hand, in the case where the target material is an elastic body, when the indenter is removed to relieve the test load, elastic recovery occurs in the vickers indentation in the direction of the arrow indicating the elastic recovery in fig. 1, with the result that the vickers indentation recovers toward the original shape to reach a permanent deformation indentation (elastic recovery). In this case, d and d 'show the relationship of d > d'.

As the degree of recovery in the direction of the arrow indicating elastic recovery in fig. 1 becomes larger, the value of the ratio of d 'to d (d'/d) becomes smaller. That is, it is shown that the elastic recovery (elastic property) is larger as the value of the ratio of d 'to d (d'/d) is smaller.

Since the conventional diamond polycrystal has a small elasticity, d and d 'are equal in length (d = d').

Since the diamond polycrystal in patent document 1 has elasticity but is small in elasticity, the value of d is substantially equal to the value of d '(d ≈ d').

On the other hand, in the diamond polycrystal of the present embodiment, the value of the ratio of d 'to d (d'/d) is 0.98 or less. Therefore, the diamond polycrystal of the present embodiment has a larger elasticity than the diamond polycrystal in patent document 1. Since the diamond polycrystal of the present embodiment has a large elasticity, the crack resistance against tensile stress is improved. Therefore, when the diamond polycrystal is used as a tool material, stress concentration on the cutting edge thereof is relieved, thereby preventing damage caused by breakage of the cutting edge.

Further, when used for cutting requiring high precision, the cutting edge of the diamond polycrystal of the present embodiment is elastically deformed, and therefore a diffraction phenomenon (so-called "iridescence pattern") which is caused by cutting marks and becomes a problem in mirror finishing is less likely to occur.

In the diamond polycrystal according to the present embodiment, the value of the ratio of d 'to d (d'/d) is 0.98 or less. When the value of the ratio (d'/d) is larger than 0.98, brittleness becomes large, and as a result, cracks are likely to occur under local stress.

The value of the ratio (d'/d) is preferably 0.97 or less, more preferably 0.9 or less. The smaller the value of the ratio (d'/d), the larger the elastic deformation becomes. If the elastic deformability becomes too large, the workability may deteriorate due to deformation of the cutting edge during machining when used as a tool. In view of this, the value of the ratio (d'/d) is preferably 0.6 or more. The value of the ratio (d'/d) is preferably 0.6 to 0.98, more preferably 0.6 to 0.97, and still more preferably 0.6 to 0.9.

In the present specification, the length d of the diagonal line in the first vickers indentation and the length d' of the diagonal line in the second vickers indentation are measured in the following manner.

In the vickers hardness test conducted under the conditions defined in JIS Z2244. Then, after the test load was released, the second vickers indentation of permanent deformation formed on the surface of the diamond polycrystal was observed with an optical microscope included in a general microhardness tester or with a laser microscope, thereby measuring the length d' of the diagonal line in the second vickers indentation.

Further, the surface of the diamond polycrystal after the test load is released is accurately observed using a high-resolution scanning electron microscope (e.g., a field emission scanning electron microscope (FE-SEM)) or a high-sensitivity differential interference microscope (a microscope that provides contrast between interference colors using interference of polarized light for the purpose of visualization).

When the surface of the diamond polycrystal was observed with a high-resolution scanning electron microscope or a high-sensitivity differential interference microscope, as shown in fig. 1, very small line-shaped indentations, which were not observed with a general optical microscope, were observed, extending from the apexes of the permanently deformed second-dimensional indentations to the outside of the second-dimensional indentations.

The length d ' of the diagonal line in the second dimensional impression and the lengths d '1 and d '2 of the linear impressions continuous with the ends of the diagonal line were measured. The length d 'of the diagonal in the second dimensional impression and the sum of the lengths d'1 and d '2 of the linear impressions (d' + d '1+ d' 2) are taken as the length d of the diagonal in the first dimensional impression.

In the diamond polycrystal of the present embodiment, the Vickers hardness calculated from the value of d is preferably 100GPa or more and less than 155GPa. Such diamond polycrystal has high hardness and may have excellent wear resistance. If the vickers hardness is less than 100GPa, cutting edge wear becomes large when the cutting tool is manufactured using, for example, diamond polycrystal, so that the cutting tool may not be used. On the other hand, if the Vickers hardness is 155GPa or more, the cutting edge is easily damaged when the cutting tool is manufactured by using a polycrystalline diamond, for example. In order to improve the wear resistance, the Vickers hardness is more preferably 120GPa or more and less than 155GPa, and still more preferably 125GPa or more and less than 140GPa.

In the present specification, vickers hardness is a value obtained based on the first dimensional indentation according to the following method. First, the length d (μm) of the diagonal line of the first vickers indentation is measured. Since the length d of the diagonal of the first dimensional indentation is measured in the above-described manner, it will not be described in detail. Vickers hardness (Hv) was calculated using the value of the length d of the diagonal line of the first dimensional indentation according to the following formula (1):

Hv＝1854.4×F/d ² formula (1)

It is to be noted that when the vickers hardness is calculated based on d' in the second dimensional indentation, the vickers hardness is an apparent hardness after elastic recovery and is larger than a value based on the intrinsic vickers hardness of the first dimensional indentation. This apparent vickers hardness does not represent the precise hardness of an industrial material on the premise of forming permanent deformation indentations as defined in JIS Z2244.

[ tools ]

The diamond polycrystal of the present embodiment has high hardness, large elasticity, excellent crack resistance, and high fracture toughness, and thus can be suitably used for cutting tools, wear-resistant tools, grinding tools, friction stir welding tools, and the like. That is, the tool of the present embodiment contains the diamond polycrystal described above.

Each of the tools shown above may be composed entirely of the diamond polycrystal, or only a part (e.g., a blade part in the case of a cutting tool) may be composed of the diamond polycrystal. Further, a coating film may be formed on the surface of each tool.

Examples of cutting tools include drills, end mills, indexable cutting inserts for drills, indexable cutting inserts for end mills, indexable cutting inserts for milling, indexable cutting inserts for turning, hacksaws, gear cutting tools, reamers, taps, cutting drills, and the like.

Examples of wear resistant tools include dies, scribers, scribing wheels, trimmers, and the like.

Examples of the abrasive tool include a grindstone and the like.

[ method for producing Diamond polycrystal ]

The diamond polycrystal can be produced, for example, by the following method.

First, a non-diamond carbon material having a graphitization degree of 0.4 or less is prepared. The non-diamond carbon material is not particularly limited as long as the non-diamond carbon material has a graphitization degree of 0.4 or less and is a carbon material other than diamond.

For example, a non-diamond carbon material in which the graphitization degree is 0.4 or less and the respective concentrations of impurities such as hydrogen, oxygen, and nitrogen are 1ppm or less can be obtained by producing the non-diamond carbon material by a thermal decomposition method from a high-purity gas.

The non-diamond carbon material is not limited to a material produced by a thermal decomposition method in a high-purity gas. Examples thereof may include: finely pulverizing graphite in a high-purity inert gas atmosphere; graphite having a low graphitization degree, such as amorphous carbon subjected to a high purity purification treatment; an amorphous carbon material; and mixtures of these.

The graphitization degree P of the non-diamond carbon material was determined as follows. The pitch d of (002) plane of graphite of the non-diamond carbon material was measured by subjecting the non-diamond carbon material to x-ray diffraction ₀₀₂ . The ratio p of turbostratic structural portions of the non-diamond carbon material was calculated according to the following formula (2):

d ₀₀₂ ＝3.440-0.086×(1-p ² ) Formula (2)

From the obtained ratio P of the turbostratic structural portion, the graphitization degree P was calculated according to the following formula (3):

p =1-P type (3)

In order to suppress the growth of crystal grains, the non-diamond carbon material preferably does not contain an iron group element metal as an impurity.

In order to suppress the growth of grains and promote direct conversion into diamond, the non-diamond carbon material preferably contains a low concentration of impurities such as hydrogen, oxygen, nitrogen, and the like. The respective concentrations of hydrogen, oxygen, and nitrogen in the non-diamond carbon material are preferably 1ppm or less, and more preferably 0.1ppm or less. Further, the total impurity concentration in the non-diamond carbon material is preferably 3ppm or less, more preferably 0.3ppm or less. In this specification, the concentration of impurities refers to a concentration based on the number of atoms.

The respective concentrations of impurities such as hydrogen, oxygen, nitrogen and the like in the non-diamond carbon material can be determined by Secondary Ion Mass Spectrometry (SIMS).

Next, assuming that P represents pressure (GPa) and T represents temperature (. Degree. C.), P and T are simultaneously increased from satisfying the conditions of T ≦ 1000 ℃ and P ≦ 10GPa to a pressure and temperature satisfying P ≧ 0.0000417T ² -0.195T +239 and P is less than or equal to 0.000096T ² -0.458t +557 and maintaining the above non-diamond carbon material at elevated pressure and temperature for more than one minute, thereby obtaining a diamond polycrystal.

When the temperature is higher than the temperature satisfying the above conditions, the grain size of the diamond grains becomes coarse regardless of the pressure, and as a result, a diamond polycrystal with high strength may not be obtained. On the other hand, when the temperature is lower than the temperature satisfying the above condition, sinterability is lowered, and as a result, the bonding strength between diamond particles may be lowered regardless of the magnitude of the pressure. The sintering time at the above pressure and temperature is preferably 5 to 20 minutes, more preferably 10 to 20 minutes.

The high-pressure high-temperature generating apparatus used in the method for producing a diamond polycrystal according to the present embodiment is not particularly limited as long as pressure and temperature conditions under which the diamond phase is a thermodynamically stable phase can be achieved; however, in order to improve productivity and workability, the high-pressure high-temperature generating device is preferably a belt type or a multi-anvil type. Further, there is no particular limitation on the storage container of the non-diamond carbon material as the raw material as long as the container is composed of a material having high pressure and high temperature resistance. For example, ta, nb, etc. are suitable.

In order to prevent impurities from entering diamond polycrystal, for example, a non-diamond carbonaceous material as a raw material is preferably vacuum-heated and sealed in a metal capsule made of a refractory metal such as Ta or Nb, and adsorbed gas and air are removed from the non-diamond carbonaceous material so as to be heated at a pressure and temperature corresponding to those described above (pressure and temperature satisfying P.gtoreq.0.0000417T) ² -0.195T +239 and P ≤ 0.000096T ² 0.458T +557 and by simultaneously increasing P and T by satisfying the conditions of T1000 ℃ and P10 Gpa, where P represents pressure (GPa) and T represents temperature (° C)), at an ultra-high pressure and temperature, directly converting the non-diamond carbon material to diamond.

[ examples ]

The present embodiment is described more specifically by way of examples below. However, the present embodiment is not limited by these examples.

Production examples 1 to 12

(production of Diamond polycrystal)

First, a raw material of a diamond polycrystal is prepared. In production examples 1 to 5 and production examples 9 to 12, non-diamond carbon materials having the graphitization degree shown in table 1 were prepared. In each of manufacturing examples 6 and 7, conventional isotropic graphite prepared by calcining graphite powder was prepared. In production example 8, a powder prepared by pulverizing graphite having a low graphitization degree and containing about 0.1% by mass of impurities (hydrogen and oxygen) into an average particle diameter of 8nm using a planetary ball mill was prepared.

Then, in each of production examples 1 to 11, the prepared raw material was vacuum-heated and sealed in a Ta-made metal capsule. The pressure was increased to 8GPa using a high-pressure high-temperature generating apparatus, then the temperature was heated to 300 ℃, and then the pressure and temperature were simultaneously increased to 17GPa and 2100 ℃ so that high-pressure high-temperature treatment was performed for 15 minutes under these pressure and temperature conditions, thereby obtaining a diamond polycrystal. It should be noted that no sintering aid or binder is added to the raw materials.

In production example 12, the prepared raw material was vacuum-heated and sealed in a Ta metal capsule. The pressure was increased to 16GPa by a high-pressure high-temperature generating apparatus, and then the temperature was heated to 2170 ℃ to perform high-pressure high-temperature treatment for 15 minutes under these pressure and temperature conditions, thereby obtaining a diamond polycrystal. It should be noted that the raw materials are not added with sintering aids and binders.

For each diamond polycrystal obtained, the average particle diameter of diamond particles, an X-ray diffraction spectrum, an impurity concentration, a value of the length d of the diagonal line of the first dimensional indentation, a value of the length d' of the diagonal line of the second dimensional indentation, vickers hardness, and a crack generation load were measured.

(average particle diameter of Diamond particles)

The average particle diameter of diamond particles contained in each diamond polycrystal was measured by an intercept method using a Scanning Electron Microscope (SEM). The specific method is as follows.

First, the polished diamond polycrystal was observed by a field emission scanning electron microscope (FE-SEM), and an SEM image was obtained.

Next, a circle is drawn on the SEM picture, and then 8 straight lines are drawn radially (in such a manner that the included angles between the straight lines are substantially equal) from the center of the circle to the outer periphery of the circle. In this case, the observation magnification and the diameter of the circle are set so that the number of diamond particles per straight line is about 10 to 50.

Then, the number of grain boundaries of the diamond particles passed through by each straight line was counted, then, the length of the straight line was divided by the number of passes to obtain an average intercept length, then the average intercept length was multiplied by 1.128, and the obtained value was regarded as an average particle diameter.

Note that the magnification of the SEM image is x30000. This is because, when the magnification is smaller than this, the number of particles in the circle increases, it becomes difficult to see the crystal grain boundary clearly, resulting in erroneous measurement of the crystal grain boundary, and there is a high possibility that the scribe line includes a plate-like structure. This is because if the magnification is larger than this, the number of particles in the circle is too small to accurately calculate the average particle diameter.

In addition, for each production example, three SEM images taken at different positions of one sample were used, and the average particle size was obtained by the above method for each SEM image, and the average of the obtained three average particle sizes was regarded as the average particle size. The results are shown in the column "average particle size of diamond particles" in Table 1.

(X-ray diffraction Spectrum)

According to the X-ray diffraction method, an X-ray diffraction spectrum of each of the obtained diamond polycrystals was obtained. Specific embodiments of the X-ray diffraction method have been described in the detailed description, and thus, will not be described in detail. In the X-ray diffraction spectrum of the diamond polycrystal in each of all the production examples, it was confirmed that there was no diffraction peak originating from a structure other than the diamond structure and the integrated intensity of the diffraction peak was more than 10% with respect to the total integrated intensity of all the diffraction peaks originating from the diamond structure.

(impurity concentration)

SIMS was used to measure the respective concentrations of nitrogen (N), hydrogen (H), and oxygen (O) in the diamond polycrystal.

In each of the diamond polycrystals of production examples 1 to 7 and production examples 9 to 12, the total amount of nitrogen, hydrogen, and oxygen was 3ppm or less. In production example 8, hydrogen and oxygen were contained in amounts of about 1000ppm, respectively.

(the length d of the diagonal of the first dimensional impression and the length d' of the diagonal of the second dimensional impression)

In the vickers hardness test performed under the conditions defined in JIS Z2244. Press vickers indenter for 10 seconds. Then, after the test load was released, the permanently deformed second vickers indents formed on the surface of the diamond polycrystalline body were observed with an optical microscope included in a general micro-hardness meter, thereby measuring the length d '(hereinafter, also referred to as "d'") of the diagonal line in the second vickers indents.

Further, the surface of the diamond polycrystal after the test load was released was observed by a field emission scanning electron microscope (FE-SEM), and the length d of the diagonal line of the first vickers impression (hereinafter, also referred to as "d") was measured.

(Vickers hardness)

From the value of the length d (μm) of the diagonal of the first dimensional indentation, vickers hardness (Hv) was calculated according to the following formula (4):

Hv＝1854.4×4.9/d ² formula (4)

The results are shown in the columns "d", "d'" and "Vickers hardness" in Table 1. Further, the value of "d '/d" is calculated from the values of "d" and "d'". The results are shown in the column "d'/d" in Table 1.

(crack initiation load)

In order to measure the crack generation load of the diamond polycrystal, a fracture strength test was conducted under the following conditions.

A spherical diamond indenter having a tip radius R of 50 μm was prepared. Each sample was loaded at room temperature (23 ℃ C. + -5 ℃ C.) at a loading rate of 1N per second. The load at the moment of crack generation (crack generation load) in the sample was measured. The instant of crack generation was measured with an AE sensor. The measurement was performed 5 times. The average of 5 values of the 5 measurements was taken as the crack generation load of each sample. The results are shown in the column "crack initiation load" in table 1. It is shown that the strength of the diamond polycrystal is higher, the crack resistance is more excellent and the fracture toughness is higher as the crack generation load is larger.

(mirror surface machining test)

In order to examine the breakage resistance of each of the tools including the diamond polycrystal of the production examples, a ball end mill tool having a diameter of 0.5mm was produced using the diamond polycrystal, and mirror-cutting of the end face of cemented carbide (WC-12% Co; particle size 0.3 μm) was performed using the same. Specific cutting conditions are as follows.

Rotating speed: 36,000rpm; cutting rate: 120mm/min; processing length: 5 μm; cutting width: 1 μm; processing time: 3.5hr; processing area: 4X 5mm.

After the cutting process, the state of the cutting edge of the tool was observed to confirm whether the cutting edge was chipped or not. Here, the state of the cutting edge "chipping" refers to a state in which a depression having a width of 0.1 μm or more or a depth of 0.01 μm or more is formed. The results are shown in the column of "edge chipping" in the "mirror surface finish test" in table 1.

After the cutting process, the state of the cutting edge of the tool was observed to measure the amount of wear of the cutting edge. Here, the "small" wear amount means that the wear amount is 0 μm or more and 5 μm or less, the "medium" wear amount means that the wear amount exceeds 5 μm and is 20 μm or less, and the "large" wear amount means that the wear amount exceeds 20 μm. The results are shown in the column entitled "wear amount" in "mirror-cutting test" in table 1.

After the cutting, the surface roughness (Ra) of the machined surface of the cemented carbide as the workpiece was measured by a laser microscope. It is shown that the smaller the value of the surface roughness (Ra), the more excellent the machined surface. The results are shown in the column "machined surface roughness Ra" in the "mirror-surface-cutting test" in table 1.

(analysis)

In each of the diamond polycrystals of production examples 1 to 5 and production examples 9 to 11, the value of the ratio (d'/d) was 0.98 or less, which corresponds to an example of the present disclosure. In each of the diamond polycrystals of production examples 6 to 8 and 12, the value of the ratio (d'/d) was more than 0.98, which corresponds to the comparative example.

It was confirmed that each of the diamond polycrystals of production examples 1 to 5 and production examples 9 to 11 had high hardness, greater crack generation load, more excellent crack resistance, and higher fracture toughness, as compared with the diamond polycrystals of production examples 6 to 8 and 12. Further, it was confirmed that according to each of the tools of production examples 1 to 5 and production examples 9 to 11, no chipping of the cutting edge occurred in the mirror-cutting machining test and the breakage resistance was excellent. It was further confirmed that according to each of the tools in production examples 1 to 5 and 9, the surface roughness of the machined surface of the workpiece was small in the mirror-cutting machining test, and the machined surface was excellent.

It was confirmed that each of the diamond polycrystals of production examples 6, 7 and 12 had high hardness, but the crack generation load was lower than that of the diamond polycrystals of production examples 1 to 5 and production examples 9 to 11, and the crack resistance and fracture toughness were poor. It was further confirmed that, according to each of the tools of production examples 6, 7 and 12, chipping of the cutting edge occurred in the mirror-cutting machining test, and the breakage resistance was poor.

It was confirmed that the diamond polycrystal of production example 8 had insufficient hardness, small crack generation load, and poor crack resistance and fracture toughness. Further, it was confirmed that the tool of production example 8 was inferior in breakage resistance, as well as chipping of the cutting edge in the mirror cutting test.

So far, the embodiments and examples of the present invention have been shown, but it is originally intended to appropriately combine the constitutions of the embodiments and examples and modify them in various ways.

The embodiments and examples disclosed herein are exemplary and non-limiting in any respect. The scope of the present invention is defined by the terms of the claims, rather than the embodiments and examples described above, and is intended to include all modifications within the scope and meaning equivalent to the terms of the claims.

Claims

1. A diamond polycrystal in which

A value of a ratio (d '/d) of d' to d in a vickers hardness test performed under conditions defined in JIS Z2244.

2. The diamond polycrystal according to claim 1, wherein the diamond polycrystal has a Vickers hardness of 100GPa or more and less than 155GPa as calculated from the value of d.

3. The diamond polycrystal according to claim 2, wherein the diamond polycrystal has a Vickers hardness of 120GPa or more and less than 155GPa as calculated from the value of d.

4. The diamond polycrystal according to any one of claims 1 to 3, wherein

The diamond polycrystal is composed of a plurality of diamond particles, and

the diamond particles have an average particle diameter of 100nm or less.

5. A tool comprising the diamond polycrystal according to any one of claims 1 to 3.